JPH03294089A - Low hydrogen type coated arc welding electrode - Google Patents
Low hydrogen type coated arc welding electrodeInfo
- Publication number
- JPH03294089A JPH03294089A JP9536590A JP9536590A JPH03294089A JP H03294089 A JPH03294089 A JP H03294089A JP 9536590 A JP9536590 A JP 9536590A JP 9536590 A JP9536590 A JP 9536590A JP H03294089 A JPH03294089 A JP H03294089A
- Authority
- JP
- Japan
- Prior art keywords
- core wire
- coating material
- amount
- strength
- added
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 238000003466 welding Methods 0.000 title claims description 61
- 239000001257 hydrogen Substances 0.000 title claims description 10
- 229910052739 hydrogen Inorganic materials 0.000 title claims description 10
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 title claims description 8
- 239000011248 coating agent Substances 0.000 claims abstract description 56
- 238000000576 coating method Methods 0.000 claims abstract description 45
- 239000000463 material Substances 0.000 claims abstract description 45
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 13
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 12
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 8
- 229910001512 metal fluoride Inorganic materials 0.000 claims abstract description 7
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 7
- 239000011230 binding agent Substances 0.000 claims abstract description 6
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 6
- 239000003381 stabilizer Substances 0.000 claims abstract description 6
- 229910052726 zirconium Inorganic materials 0.000 claims abstract description 5
- -1 alkaline earth metal Chemical compound 0.000 claims abstract description 3
- 229910052784 alkaline earth metal Inorganic materials 0.000 claims abstract 2
- 229910052751 metal Inorganic materials 0.000 abstract description 44
- 239000002184 metal Substances 0.000 abstract description 44
- BVKZGUZCCUSVTD-UHFFFAOYSA-L Carbonate Chemical compound [O-]C([O-])=O BVKZGUZCCUSVTD-UHFFFAOYSA-L 0.000 abstract description 6
- 239000003795 chemical substances by application Substances 0.000 abstract description 3
- 150000001342 alkaline earth metals Chemical class 0.000 abstract 1
- 239000002893 slag Substances 0.000 description 18
- 229910000831 Steel Inorganic materials 0.000 description 16
- 239000000306 component Substances 0.000 description 16
- 239000010959 steel Substances 0.000 description 16
- 230000000694 effects Effects 0.000 description 15
- 239000011324 bead Substances 0.000 description 9
- 238000010438 heat treatment Methods 0.000 description 8
- 238000001556 precipitation Methods 0.000 description 8
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 7
- 230000007423 decrease Effects 0.000 description 5
- 230000007774 longterm Effects 0.000 description 5
- 150000001247 metal acetylides Chemical class 0.000 description 5
- 235000019353 potassium silicate Nutrition 0.000 description 5
- NTHWMYGWWRZVTN-UHFFFAOYSA-N sodium silicate Chemical compound [Na+].[Na+].[O-][Si]([O-])=O NTHWMYGWWRZVTN-UHFFFAOYSA-N 0.000 description 5
- 238000012360 testing method Methods 0.000 description 5
- 238000007792 addition Methods 0.000 description 4
- AYJRCSIUFZENHW-UHFFFAOYSA-L barium carbonate Chemical compound [Ba+2].[O-]C([O-])=O AYJRCSIUFZENHW-UHFFFAOYSA-L 0.000 description 4
- 230000015572 biosynthetic process Effects 0.000 description 4
- 229910052799 carbon Inorganic materials 0.000 description 4
- 238000005336 cracking Methods 0.000 description 4
- 239000007789 gas Substances 0.000 description 4
- 239000010936 titanium Substances 0.000 description 4
- 229910052719 titanium Inorganic materials 0.000 description 4
- 230000000052 comparative effect Effects 0.000 description 3
- 230000006866 deterioration Effects 0.000 description 3
- 229910052742 iron Inorganic materials 0.000 description 3
- 238000002844 melting Methods 0.000 description 3
- 230000008018 melting Effects 0.000 description 3
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 2
- VTYYLEPIZMXCLO-UHFFFAOYSA-L Calcium carbonate Chemical compound [Ca+2].[O-]C([O-])=O VTYYLEPIZMXCLO-UHFFFAOYSA-L 0.000 description 2
- 239000004111 Potassium silicate Substances 0.000 description 2
- 239000004115 Sodium Silicate Substances 0.000 description 2
- 229910045601 alloy Inorganic materials 0.000 description 2
- 239000000956 alloy Substances 0.000 description 2
- QVGXLLKOCUKJST-UHFFFAOYSA-N atomic oxygen Chemical compound [O] QVGXLLKOCUKJST-UHFFFAOYSA-N 0.000 description 2
- 239000008358 core component Substances 0.000 description 2
- 238000011161 development Methods 0.000 description 2
- 238000005538 encapsulation Methods 0.000 description 2
- 239000012535 impurity Substances 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 230000003647 oxidation Effects 0.000 description 2
- 238000007254 oxidation reaction Methods 0.000 description 2
- 239000001301 oxygen Substances 0.000 description 2
- 229910052760 oxygen Inorganic materials 0.000 description 2
- NNHHDJVEYQHLHG-UHFFFAOYSA-N potassium silicate Chemical compound [K+].[K+].[O-][Si]([O-])=O NNHHDJVEYQHLHG-UHFFFAOYSA-N 0.000 description 2
- 229910052913 potassium silicate Inorganic materials 0.000 description 2
- 239000002244 precipitate Substances 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- 230000004044 response Effects 0.000 description 2
- 229910052710 silicon Inorganic materials 0.000 description 2
- 229910052911 sodium silicate Inorganic materials 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- GWEVSGVZZGPLCZ-UHFFFAOYSA-N titanium dioxide Inorganic materials O=[Ti]=O GWEVSGVZZGPLCZ-UHFFFAOYSA-N 0.000 description 2
- 241000473391 Archosargus rhomboidalis Species 0.000 description 1
- 229910000640 Fe alloy Inorganic materials 0.000 description 1
- 229910002551 Fe-Mn Inorganic materials 0.000 description 1
- 229910002593 Fe-Ti Inorganic materials 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
- 238000005054 agglomeration Methods 0.000 description 1
- 230000002776 aggregation Effects 0.000 description 1
- 229910000019 calcium carbonate Inorganic materials 0.000 description 1
- 235000010216 calcium carbonate Nutrition 0.000 description 1
- WUKWITHWXAAZEY-UHFFFAOYSA-L calcium difluoride Chemical compound [F-].[F-].[Ca+2] WUKWITHWXAAZEY-UHFFFAOYSA-L 0.000 description 1
- 150000004649 carbonic acid derivatives Chemical class 0.000 description 1
- 230000008859 change Effects 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- 230000002950 deficient Effects 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000011156 evaluation Methods 0.000 description 1
- 239000000835 fiber Substances 0.000 description 1
- 238000010304 firing Methods 0.000 description 1
- 229910052731 fluorine Inorganic materials 0.000 description 1
- 150000002222 fluorine compounds Chemical class 0.000 description 1
- 239000010436 fluorite Substances 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 238000011835 investigation Methods 0.000 description 1
- 235000012204 lemonade/lime carbonate Nutrition 0.000 description 1
- PAZHGORSDKKUPI-UHFFFAOYSA-N lithium metasilicate Chemical compound [Li+].[Li+].[O-][Si]([O-])=O PAZHGORSDKKUPI-UHFFFAOYSA-N 0.000 description 1
- 229910052912 lithium silicate Inorganic materials 0.000 description 1
- 150000002739 metals Chemical class 0.000 description 1
- 229910052698 phosphorus Inorganic materials 0.000 description 1
- 238000002360 preparation method Methods 0.000 description 1
- 230000008569 process Effects 0.000 description 1
- 230000001737 promoting effect Effects 0.000 description 1
- 230000001681 protective effect Effects 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 230000006641 stabilisation Effects 0.000 description 1
- 238000011105 stabilization Methods 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
- 238000005496 tempering Methods 0.000 description 1
- 229910000999 vanadium-gallium Inorganic materials 0.000 description 1
Landscapes
- Nonmetallic Welding Materials (AREA)
Abstract
Description
【発明の詳細な説明】
（産業上の利用分野）
本発明はＣｒ −Ｍｏ系高温用鋼用溶接材料、詳しくは
２′／４Ｃｒ−ＩＭｏ及び３ Ｃｒ −］ Ｍｏａ等の
Ｃｒ −Ｍｏ系高温用鋼を対象とし、長時間熱処理後で
も高温特性に優れた溶接金属を得る低水素系被覆アーク
溶接棒に関するものである。Detailed Description of the Invention (Field of Industrial Application) The present invention relates to welding materials for Cr-Mo high-temperature steels, specifically Cr-Mo high-temperature welding materials such as 2'/4Cr-IMo and 3Cr-] Moa. This invention relates to a low-hydrogen coated arc welding rod for steel that produces weld metal with excellent high-temperature properties even after long-term heat treatment.
（従来の技術）
近年、石油精製プラント等の操業効率を高めるため、そ
れに使用される圧力容器の大型化あるいは操業温度の高
温化が要求されてきている。(Prior Art) In recent years, in order to improve the operational efficiency of oil refining plants and the like, there has been a demand for larger pressure vessels or higher operating temperatures for the pressure vessels used therein.
このような要求に対し、母材については高温用鯛の高強
度化がすでに進められてきている。一方、これら高強度
母材の溶接に用いられる被覆アーク溶接棒による溶接金
属についても同様であり、長時間熱処理後でも優れた高
温特性を有する溶接金属を得る被覆アーク溶接棒の開発
が要望されている。In response to these demands, efforts have already been made to increase the strength of the base material of high-temperature sea bream. On the other hand, the same applies to the weld metal produced by coated arc welding rods used for welding these high-strength base materials, and there is a demand for the development of coated arc welding rods that can produce weld metal with excellent high-temperature properties even after long-term heat treatment. There is.
このような状況に対し、特開昭５９−１７８１９７号公
報では、心線中のＣ，Ｓｉ、 Ｍｎ、 Ｃｒ、 Ｍｏ、
Ｖの添加量を限定すると同時に、この心線にＣａＣ０
ｚ、 ＣａＦ。In response to this situation, JP-A-59-178197 discloses that C, Si, Mn, Cr, Mo,
At the same time as limiting the amount of V added, CaC0 is added to this core wire.
z, CaF.
を必須成分とする被覆剤を塗布したことを特徴とする高
温用鋼用被覆アーク溶接材料が開示されているが、これ
は高Ｃｒ鋼と低Ｃｒ鋼とを溶接する際に、高Ｃｒ側の溶
接ボンド部における溶接後熱処理時の組織変化を抑制し
、健全な異材溶接部を得るためのものであって、高温強
度およびクリープ破断強度などの高温特性を積極的に向
上させようとするものではなく、高温特性に優れた２％
〜３％Ｃｒ −１％ＭＯ鋼用被履用被覆アーク溶接棒す
るに至っていない。また、特開昭６０−４０６８９号公
報は、被覆剤成分としてＣａＣＯ３，金属弗化物＋ ５
ｔＯ２＋ ｓｉ、 Ｍｇを必須成分とし、かつ心線含有
量との関係でＴｉ０ｚ。A coated arc welding material for high-temperature steel is disclosed, which is characterized by being coated with a coating agent containing as an essential component. It is intended to suppress structural changes during post-weld heat treatment at the weld bond and to obtain a healthy dissimilar metal weld, and is not intended to actively improve high-temperature properties such as high-temperature strength and creep rupture strength. 2% with excellent high-temperature properties.
~3%Cr -1%MO It has not yet reached the point where it can be used as a coated arc welding rod for steel. Furthermore, JP-A No. 60-40689 discloses that CaCO3, metal fluoride + 5
tO2+ si, Mg is an essential component, and Ti0z in relation to the core fiber content.
（：、、 Ｍｎ、 Ｃｒ、 Ｍｏ、 Ｖを添加し得る任
意成分とからなる被覆剤を心線成分としてＣ，Ｓｔ、
Ｍｎ、 Ｃｒ、 Ｍｏ。(:, Mn, Cr, Mo, a coating material consisting of an arbitrary component that can be added with V as a core component, C, St,
Mn, Cr, Mo.
Ｔｉ、 Ｖを限定し、残部がＦｅ及び不可避不純物から
なる心線に、粘結剤として硅酸ソーダ、硅酸カリ及び硅
酸リチウムなどの混合物を用いて被覆せしめた被覆アー
ク溶接棒により、Ｃｒ −Ｍｏ系高温用鋼をアーク溶接
し、更に溶接金属成分としてＣ，Ｓｉ。A coated arc welding rod in which Ti and V are limited, and the remainder is Fe and unavoidable impurities is coated with a mixture of sodium silicate, potassium silicate, lithium silicate, etc. as a binder. -Mo-based high-temperature steel is arc welded, and C and Si are further added as weld metal components.
Ｍｎ、 Ｃｒ、 Ｍｏ、 Ｔｉ、 Ｖを含ませること
により、特に低温靭性に優れたＣｒ −Ｍｏ系高温用鋼
のアーク溶接方法を開示しているが、高温強度およびク
リープ破断強度を積極的に向上しようというものではな
く、高温特性に優れた２Ｘ〜３％Ｃｒ−１％Ｍｏ鋼用被
覆アーク溶接棒を提供するに至っていない。Discloses an arc welding method for Cr-Mo high-temperature steel, which has particularly excellent low-temperature toughness by containing Mn, Cr, Mo, Ti, and V, but actively improves high-temperature strength and creep rupture strength. However, a coated arc welding rod for 2X to 3% Cr-1% Mo steel with excellent high-temperature properties has not yet been provided.
前記問題点に対し、本発明者らが特開昭６２−２２４４
９７号公報ですでに提案している如く、溶接金属中の炭
化物の過剰生成によるＣの減少を起さない範囲でＶを添
加することにより高強度化を計るとともに、溶接金属に
微細なＶ、Ｃ，を析出させ、ＭｚｓＣｈ、 Ｍ６Ｃの析
出状態を長時間にわたって粗大化しないようコントロー
ルし、長時間熱処理後でも４５０〜５００℃における高
温強度およびクリープ破断強度の維持向上が可能である
ことを見出している。しかしながら、高温強度およびク
リープ破断強度は圧力容器などを設計する上で重要な特
性であることからその安全性を高めるためには更に高温
強度及びクリープ破断強度などの高温特性の向上を計る
必要がある。In order to solve the above-mentioned problems, the present inventors have proposed
As already proposed in Publication No. 97, high strength can be achieved by adding V within a range that does not cause a decrease in C due to excessive formation of carbides in the weld metal, and fine V, We discovered that it is possible to precipitate C, and control the precipitation state of MzsCh and M6C so that they do not become coarse over a long period of time, and maintain and improve high-temperature strength and creep rupture strength at 450 to 500°C even after long-term heat treatment. There is. However, since high-temperature strength and creep rupture strength are important properties when designing pressure vessels, it is necessary to further improve high-temperature properties such as high-temperature strength and creep rupture strength in order to increase their safety. .
（発明が解決しようとする課題）
本発明は２ｚ〜３％Ｃｒ−１％ＨＯ鋼の溶接において、
安全性の高い優れた高温特性を有する溶接金属を得る低
水素系被覆アーク溶接棒を提供することを目的とするも
のである。(Problems to be Solved by the Invention) The present invention provides for welding 2z to 3% Cr-1% HO steel.
The object of the present invention is to provide a low-hydrogen coated arc welding rod that yields a weld metal that is highly safe and has excellent high-temperature properties.
（課題を解決するための手段）
本発明の要旨とするところは、心線または被覆剤のいず
れか一方あるいは両方に必須としてＴａ、その他にＭｎ
、 Ｃｒ、 Ｍｏ、 Ｖ、 ＮｂおよびＺｒの一種ま
たは二種以上を重置％で
Ｔａ二０．０１≦心線中（Ｔａ）
＋被覆剤中（Ｔａ） Ｘ ０．２０≦５．０Ｍｎ ：
０．１≦心線中（Ｍｎ）
＋被覆剤中（Ｍｎ） Ｘ ０．１５≦１．５Ｃｒ ：
２．０≦心線中（Ｃｒ）
＋被覆剤中（Ｃｒ） Ｘ ０．３５≦３．５Ｍｏ ：
０．８≦心線中（ＭＯ）
十被覆剤中（Ｍｏ） Ｘ ０．３５≦１．５Ｖ ： ０
．４≦心線中（Ｖ）
十被覆剤中（Ｖ）×０．２８≦１． ＯＮｂ：０．０２
≦心線中（Ｎｂ）
十被覆剤中（Ｎｂ） Ｘ ０．２０≦０．１１Ｚｒ：０
．０５≦心線中（Ｚｒ）
＋被覆剤中（Ｚｒ）×０．５≦１．０
の範囲で添加し、被覆剤全重量に対しアルカリ土類金属
の炭酸塩を３０〜７０％、金属弗化物を５〜３０％、Ｍ
ｇ０．５〜５％、その他に上記以外の脱酸剤、アーク安
定剤、粘結剤を含む被覆剤を心線の周囲に被覆したこと
を特徴とする低水素系被覆アーク溶接棒にある。(Means for Solving the Problems) The gist of the present invention is to provide Ta as an essential component in either or both of the core wire and the coating material, and in addition to Mn.
, Cr, Mo, V, Nb and Zr in a superposition percentage of Ta2 0.01≦(Ta) in the core + (Ta) in the coating material X 0.20≦5.0Mn:
0.1≦core (Mn) + coating material (Mn) X 0.15≦1.5Cr:
2.0≦core (Cr) + coating material (Cr) X 0.35≦3.5Mo:
0.8≦In the core (MO) In the coating agent (Mo) X 0.35≦1.5V: 0
．． 4≦core wire (V) 10 coating material (V)×0.28≦1. ONb: 0.02
≦In the core (Nb) In the coating agent (Nb) X 0.20≦0.11Zr:0
．． 05≦(Zr) in the core wire + (Zr) in the coating material x 0.5≦1.0. 5-30% of compounds, M
The present invention provides a low hydrogen-based coated arc welding rod characterized in that the core wire is coated with a coating material containing 0.5 to 5% g0.5 to 5% and a deoxidizing agent, an arc stabilizer, and a binder other than those mentioned above.
なお、本発明で用いる心線は、Ｔａ、 Ｍｎ、 Ｃｒ、
Ｍｏ。Note that the core wire used in the present invention includes Ta, Mn, Cr,
Mo.
Ｖ、 Ｎｂ、 Ｚｒ以外の化学成分がＣ： ０．１６％
以下Ｓｉ：０．２５％以下、Ｐ ： ０．０２％以下、
Ｓ ： ０．０２％以下、残部がＦｅおよび不可避不純
物から成るものである。Chemical components other than V, Nb, and Zr are C: 0.16%
Below Si: 0.25% or less, P: 0.02% or less,
S: 0.02% or less, the remainder consisting of Fe and inevitable impurities.
２Ｘ〜３％Ｃｒ−１％ＭＯ鋼の溶接において、溶接金属
の高温強度およびクリープ破断強度の低下原因は、溶接
金属が高温に長時間加熱される過程、すなわち長時間熱
処理の過程においてまず、溶接金属中のＣとＦｅが結合
してＦｅ、Ｃを析出し、次にこの炭化物がＭｚｘＣｈ、
ＭＭＣ（Ｍは金属元素を指す）に変化し、炭化物が粗
大化することによるものとされている。When welding 2X to 3% Cr-1% MO steel, the cause of the decline in the high temperature strength and creep rupture strength of the weld metal is that the weld metal is heated to a high temperature for a long time, that is, in the process of long-term heat treatment. C and Fe in the metal combine to precipitate Fe and C, and then this carbide becomes MzxCh,
This is thought to be caused by the change to MMC (M refers to a metal element) and the coarsening of carbides.
そこで本発明者らは鋭意研究の結果、溶接金属中の炭化
物の過剰生成によるＣの減少を起さない範囲で■を添加
することにより溶接金属に微細なＶ４Ｃｓを析出させ、
ＭｚｘＣｈ、 ＭａＣの析出状態を長時間にわたって粗
大化しないようコントロールすることを基本技術として
、更に溶接棒中にＴａを添加して溶接金属にＴａＣを析
出させることにより長時間熱処理後でも４５０〜５００
℃において、高温強度、高温延性およびクリープ破断強
度などの高温特性をより一層向上できることを見出した
。Therefore, as a result of intensive research, the present inventors have determined that fine V4Cs can be precipitated in the weld metal by adding (■) within a range that does not cause a decrease in C due to excessive formation of carbides in the weld metal.
The basic technology is to control the precipitation state of MzxCh, MaC so that it does not become coarse over a long period of time, and by adding Ta to the welding rod to precipitate TaC in the weld metal, even after long heat treatment, the
It has been found that high-temperature properties such as high-temperature strength, high-temperature ductility, and creep rupture strength can be further improved at ℃.
本発明はかかる知見に基づいてなされたものであり、以
下に作用と共に本発明の詳細な説明する。The present invention has been made based on this knowledge, and the present invention will be described in detail below along with its functions.
（作 用）
本発明の最大の特徴は、高温特性のより一層の向上と安
定化に対し、溶接棒中にＴａを添加すること、すなわち
溶接して得られる２Ｘ〜３％Ｃｒ−１％Ｍｏ鋼溶接金属
にＴａＣを析出させ４５０〜５００℃での高温強度、高
温延性およびクリープ破断強度を格段に高め、高温特性
の安定化を計ることにある。(Function) The greatest feature of the present invention is that Ta is added to the welding rod for further improvement and stabilization of high-temperature properties, that is, 2X to 3%Cr-1%Mo obtained by welding. The purpose is to precipitate TaC in steel weld metal to significantly increase high temperature strength, high temperature ductility and creep rupture strength at 450 to 500°C, and to stabilize high temperature properties.
第１図は、炭酸石灰５５．０％、蛍石１９．０％、炭酸
バリウム４６０％、Ｆｅ−５ｔ （Ｓｉ分４５％）７．
５％、金属Ｍｎ２．０％、金属Ｍｇ１．５％、粘結剤９
．５％、残部が塗装助剤、鉄粉からなる被覆剤を、Ｃ０
，０５〜０．１６％、Ｓｔ ０．０４〜０．２４％、Ａ
ｎ０．１１〜１．４８％、Ｃｒ ２．０２〜３．４４％
、Ｍ。Figure 1 shows lime carbonate 55.0%, fluorite 19.0%, barium carbonate 460%, Fe-5t (Si content 45%)7.
5%, metal Mn 2.0%, metal Mg 1.5%, binder 9
．． A coating agent consisting of 5%, the balance being a coating aid and iron powder, was coated with C0
, 05-0.16%, St 0.04-0.24%, A
n0.11-1.48%, Cr 2.02-3.44%
,M.
０．８１〜１．４４％、Ｖｏ、４１〜０．９９％、Ｎｂ
０．０２１〜０．１％を添加し、かつＴａの添加量を変
化させた直径４．０閣、長さ４００■の心線に、被覆外
径６．３■に被覆塗装した後に乾燥、焼成して被覆アー
ク溶接棒を製造し、ＡＷＳ＾５．４に準じて溶接し、短
時間高温引張強度、およびクリープ破断試験を実施した
結果を示すものであり、第１表の結果から被覆アーク溶
接棒として心線または被覆剤のいづれか一方あるいは両
方に添加するＴａ量と短時間高温引張強度、高温延性お
よびクリープ破断強度との関係を図示したものである。0.81-1.44%, Vo, 41-0.99%, Nb
A core wire with a diameter of 4.0 cm and a length of 400 cm, to which 0.021 to 0.1% of Ta was added and the amount of Ta added was varied, was coated to an outer diameter of 6.3 cm, and then dried. This shows the results of firing a coated arc welding rod, welding it in accordance with AWS^5.4, and conducting short-time high temperature tensile strength and creep rupture tests. This figure illustrates the relationship between the amount of Ta added to either or both of the core wire and the coating material of the welding rod and the short-time high temperature tensile strength, high temperature ductility, and creep rupture strength.
また、この場合の溶接施行条件は、予熱、パス間・温度
２００〜２５０°Ｃ１電流１６０Ａ、溶接入熱２５ｋＪ
／ｃ１１なる条件で溶着金属を作成した。また、溶着金
属は溶接後７１０℃、３０ｈｒの後熱処理を施した後に
短時間高温引張試験片及びクリープ破断試験片を採取し
、短時間高温引張試験は４８２℃での引張強度および伸
び率、クリープ破断試験は５００℃、３０００ｈｒ時の
破断強度をそれぞれ求めたものである。In addition, the welding conditions in this case are preheating, inter-pass temperature 200-250°C, current 160A, and welding heat input 25kJ.
Weld metal was prepared under the following conditions: /c11. In addition, the weld metal was subjected to post-heat treatment at 710℃ for 30 hours after welding, and short-time high temperature tensile test pieces and creep rupture test pieces were taken. In the breaking test, the breaking strength was determined at 500° C. for 3000 hours.
なお、第１表の総合判定は、 ○印；良好 Δ印；やや良好 ×印；不良 を示す。The overall judgment in Table 1 is as follows: ○ mark; good Δ mark; somewhat good × mark; defective shows.
その結果、被覆アーク溶接棒として心線中または被覆剤
のいずれか一方あるいは両方へ適量のＴａを添加するこ
とにより、良好な短時間高温引張強度、・高温延性およ
びクリープ破断強度の得られることが判明した。As a result, by adding an appropriate amount of Ta to either the core wire or the coating material, or both, as a coated arc welding rod, good short-time high temperature tensile strength, high temperature ductility, and creep rupture strength can be obtained. found.
第１表および第１図の結果から明らかな如く、被覆アー
ク溶接棒として心線または被覆剤のいづれか一方あるい
は両方に添加するＭｎ、 Ｃｒ、 Ｍｏ、 ＶおよびＮ
ｂ量が本発明の要件を満たしていてもＴａ量が０．０１
％未満のもの？４１１１〜に２．随８〜阻９は短時間高
温引張強度が５４ｋｇ／−未満、クリープ破断強度が３
３ｋｇ／−未満と低かったり、Ｔａ量が５．０％を超え
るもの胤１７〜黒１８．魔２４〜患２５は短時間高温引
張伸び率が２０％未満と高温延性の劣化が認められてお
り、被覆アーク溶接棒として心線中または被覆剤のいづ
れか一方あるいは両方に添加するＴａ量を０．０１〜５
．０％の範囲にする必要のあることが判明した。以下、
本発明における各成分の作用と成分範囲限定の理由を述
べる。As is clear from the results in Table 1 and Figure 1, Mn, Cr, Mo, V, and N added to either the core wire or the coating material, or both, as a coated arc welding rod.
Even if the b amount satisfies the requirements of the present invention, the Ta amount is 0.01
Anything less than %? 4111～2. Items 8 to 9 have a short-time high temperature tensile strength of less than 54 kg/- and a creep rupture strength of 3.
Seeds 17 to black 18. Those with a low weight of less than 3 kg/- or with a Ta content of more than 5.0%. In 24 to 25, the short-time high temperature tensile elongation rate was less than 20% and the deterioration of high temperature ductility was observed. .01~5
．． It was found that it was necessary to keep it in the 0% range. below,
The effect of each component in the present invention and the reason for limiting the range of the components will be described.
（Ｔａ： ０．０１≦心線中（Ｔａ）十被覆剤中（Ｔａ
） Ｘ０１２０≦５．０〕
Ｔａは高温強度およびクリープ破断強度を著しく高める
成分であり、ＴａＣが析出し特に高温長時間側でのクリ
ープ破断強度向上への効果は極めて大赤い、しかしなが
ら０．０１％未満ではその効果が得られない、他方、５
．０％を超えると靭性が大幅に劣化してくるので上限を
５．０％とした。(Ta: 0.01≦(Ta) in the core wire (Ta) in the coating material (Ta)
) On the other hand, if it is less than 5, the effect cannot be obtained.
．． If it exceeds 0%, the toughness will deteriorate significantly, so the upper limit was set at 5.0%.
（Ｍｎ：０．１≦心線中０１ｎ）十被覆剤中（Ｍｎ）
×０．１５≦１．５〕
Ｍｎは溶接金属中の酸素量低減に有効であると同時に、
鋼の焼入れ性を向上させ強度維持に不可欠の成分である
が、０．１％未満ではその作用効果が得られない、他方
、１．５％を超えると高温における強度および耐酸化性
を低下させるので１．５％を上限とした。(Mn: 0.1≦01n in core wire) (Mn) in coating agent
×0.15≦1.5] Mn is effective in reducing the amount of oxygen in the weld metal, and at the same time,
It is an essential component to improve the hardenability of steel and maintain its strength, but if it is less than 0.1%, its effects cannot be obtained.On the other hand, if it exceeds 1.5%, it reduces the strength and oxidation resistance at high temperatures. Therefore, the upper limit was set at 1.5%.
［Ｃｒ：２．０≦心線中（Ｃｒ）十被覆剤中（Ｃｒ）
×０．３５≦３．５〕
Ｃｒは高温環境化での耐酸化性を確保するために不可欠
の成分であって、耐熱鋼にはその用途に合わせ適量のＣ
ｒが必らず添加されており、Ｍ！ｊＣ６ＴＭ＆Ｃ（但し
Ｍは金属元素を示す）の微細析出により、特に高温強度
を高めている。しかし、その量が２．０％未滴では十分
な強度が確保できない。他方、３．５％を超えると適用
鋼材のＣｒ量に合致しなくなるので３．５％を上限とし
た。[Cr: 2.0≦(Cr) in core wire (Cr) in coating material
×0.35≦3.5] Cr is an essential component to ensure oxidation resistance in high-temperature environments, and heat-resistant steel contains an appropriate amount of C depending on its use.
r is always added, and M! The fine precipitation of jC6TM&C (where M represents a metal element) particularly enhances the high temperature strength. However, if the amount is 2.0%, sufficient strength cannot be ensured. On the other hand, if it exceeds 3.5%, it will not match the Cr content of the applied steel material, so 3.5% is set as the upper limit.
（Ｍｏ：０．８≦心線中（ＨＯ）十被覆剤中（Ｍｏ）
×０．３５≦１．５〕
Ｎｏはクリープ破断強度を高める成分であるが、０．８
％未満ではその効果が得られない、他方、１．５％を超
えると焼戻し脆化特性が劣化するので１．５％を上限と
した。(Mo: 0.8≦(HO) in the core wire (Mo) in the coating material (Mo)
×0.35≦1.5] No is a component that increases creep rupture strength, but 0.8
If the content is less than 1.5%, the effect cannot be obtained. On the other hand, if it exceeds 1.5%, the tempering embrittlement properties deteriorate, so 1.5% is set as the upper limit.
（Ｖ：０．４≦心線中（Ｖ）十被覆剤中（■）×０．２
８≦１．０）
■は高温強度を著しく高める成分であり、析出の場合に
は、Ｖ３Ｇａとしての他、ＬｓＣｉ、 ＮｂＣの一部に
入り析出物の粗大化の抑制に優れた効果を発揮するが、
０．４％未満では所望の効果を得ることができない、他
方、１．０％を超えると炭化物の生成過剰を招き、溶接
金属中のＣが減少し、逆に強度の低下をきたすと同時に
スラグの剥離性が劣化するので１．０％を上限とした。(V: 0.4≦(V) in core wire (■) in coating material (■)×0.2
8≦1.0) ■ is a component that significantly increases high-temperature strength, and in the case of precipitation, it enters not only as V3Ga but also as a part of LsCi and NbC and has an excellent effect on suppressing the coarsening of precipitates. but,
If it is less than 0.4%, the desired effect cannot be obtained. On the other hand, if it exceeds 1.0%, it will lead to excessive formation of carbides, reduce C in the weld metal, and conversely cause a decrease in strength, as well as slag formation. The upper limit was set at 1.0% because the releasability of the film deteriorates.
［Ｎｂ：０．０２≦心線中（Ｎｂ）十被覆剤中（Ｎｂ）
ｘｏ、２０≦０．１１３
ＮｂはＮｂＣの析出によって高温強度を高め、後続する
微細な分散析出物であるＨｚｓＣｈ、 Ｉ’ｌａＣ等の
析出状態を微細にコントロールするために高温長時間ク
リープ強度改善に効果がある。しかしその量が０．０２
％未満ではその効果がなく、０．１１％を超えると凝集
粗大化を生じ強度を低下させるため下限を０．０２％、
上限を０．１１％とした。[Nb: 0.02≦(Nb) in the core wire (Nb) in the coating material
xo, 20≦0.113 Nb improves high-temperature strength by precipitation of NbC, and improves high-temperature long-term creep strength to finely control the precipitation state of subsequent fine dispersed precipitates such as HzsCh and I'laC. effective. However, the amount is 0.02
If it is less than 0.1%, there is no effect, and if it exceeds 0.11%, it will cause agglomeration and coarsening and reduce the strength, so the lower limit is set at 0.02%,
The upper limit was set at 0.11%.
（Ｚｒ：０．０５≦心線中（Ｚｒ）十被覆剤中（Ｚｒ）
×０．５≦１．０〕
Ｚｒは強力な脱酸剤としての作用効果と、溶接金属結晶
粒の微細化に有効であるが、その量が０．０５％未満で
はその効果がなく、１．０％を超えると溶接作業性が著
しく悪化してくるので１．０％を上限とした。(Zr: 0.05≦In the core wire (Zr) 10 In the coating agent (Zr)
×0.5≦1.0] Zr has the effect of acting as a strong deoxidizing agent and is effective in refining the weld metal crystal grains, but if the amount is less than 0.05%, it has no effect; If it exceeds 0.0%, welding workability will be significantly deteriorated, so 1.0% is set as the upper limit.
すなわちＴａ以外の選択成分については心線のみに添加
する場合は、Ｈｎ ： ０．１〜１．５％、Ｃｒ：１０
〜３．５％、 Ｎｏ： ０．８〜１．５％、Ｖ：Ｑ、４
〜１．０％、Ｎｂ：０．０２〜０．１１％、 Ｚｒ：
０．０５〜１．０％。That is, when adding selected components other than Ta only to the core wire, Hn: 0.1 to 1.5%, Cr: 10
~3.5%, No.: 0.8~1.5%, V:Q, 4
~1.0%, Nb: 0.02~0.11%, Zr:
0.05-1.0%.
被覆剤のみに添加する場合は、Ｍｎ：０．６７〜１０％
、 Ｃｒ ： ５．７〜１０．０％、 Ｍｏ ：１２９
〜４．２９％。When added only to the coating material, Mn: 0.67 to 10%
, Cr: 5.7-10.0%, Mo: 129
~4.29%.
Ｖ ： １．４３〜３．５７％、Ｎｂ：０．１〜０．５
５％、 Ｚｒ二０．１〜２．．０％、心線と被覆剤の両
方から添加する場合は、上記式の範囲内であれば任意の
割合で選定できる。V: 1.43-3.57%, Nb: 0.1-0.5
5%, Zr2 0.1-2. ．． 0%, and when adding from both the core wire and the coating material, any ratio can be selected as long as it is within the range of the above formula.
〔金属炭酸塩：３０〜７０重量％〕
本発明でいう金属炭酸塩とはＣａＣＯ５＋ ＢａＣＯ３
゜ＭｇＣＯ５などを指すが、これらの金属炭酸塩はアー
ク中で分解することによりＣ０ｗガスを発生し、溶融金
属を大気から遮断保護するとともにアーク雰囲気中の水
素、窒素のガス分圧を下げる効果がある。これらの添加
量が３０％未満ではスラグの融点が低下するためスラグ
の被包性が悪くなって良好な溶接ビード外観、形状を得
ることが出きない、また、ＣＯｔガスの発生量が不足す
るためビットやブローホールが発生したり、溶接金属中
の水素量が増加し、耐低温割れ性が劣化してくる。他方
、７０％を超えるとガス発生量が過剰となるためビット
が多発する。また、スラグの融点が上昇してスラグの流
動性が悪くなり、溶接ビード外観。[Metal carbonate: 30-70% by weight] The metal carbonate referred to in the present invention is CaCO5+ BaCO3
゜These metal carbonates, such as MgCO5, generate C0w gas by decomposing in the arc, which protects the molten metal from the atmosphere and has the effect of lowering the gas partial pressure of hydrogen and nitrogen in the arc atmosphere. be. If the amount of these additions is less than 30%, the melting point of the slag decreases, resulting in poor slag encapsulation, making it impossible to obtain a good weld bead appearance and shape, and in addition, the amount of COt gas generated is insufficient. As a result, bits and blowholes occur, the amount of hydrogen in the weld metal increases, and cold cracking resistance deteriorates. On the other hand, if it exceeds 70%, the amount of gas generated will be excessive and bits will occur frequently. In addition, the melting point of the slag increases and the fluidity of the slag deteriorates, resulting in the appearance of weld beads.
形状が劣化してくるので７０％を上限とした。Since the shape deteriorates, the upper limit was set at 70%.
〔金属弗化物：５〜３０重量％〕
本発明でいう金属弗化物とはＣａＦ＊＋ Ｂａ５ｓｓ
ＭｇＦ露＋ＬｉＦ、ＡｊＦｌなどを指すが、いずれもス
ラグの融点を低下させるため溶接中のスラグ流動性を良
好にする。また、アーク中で分解した弗化物は溶融金属
や溶融スラグの水素と反応し、溶接金属中の水素量を低
下させ耐低温割れ性の良好な溶接金属をつくる。これら
の添加量が５％未満では、適当なスラグの流動性が得ら
れないため溶接ビード外観。[Metal fluoride: 5 to 30% by weight] The metal fluoride in the present invention is CaF*+ Ba5ss
MgF dew + LiF, AjFl, etc., all of which lower the melting point of slag and improve slag fluidity during welding. In addition, fluorides decomposed in the arc react with hydrogen in the molten metal and molten slag, reducing the amount of hydrogen in the weld metal and creating a weld metal with good cold cracking resistance. If the amount of these additives is less than 5%, appropriate slag fluidity cannot be obtained, resulting in a weld bead appearance.
形状が劣化すると同時にビットが発生し易く、また溶接
金属中の水素量が増加して耐低温割れ性が著しく劣化し
てくる。他方、３０％を超えるとスラグの粘性が不足す
るため溶接ビード外観、形状が悪くなったり、また保護
筒が脆弱になり溶接作業性が劣化してくるので３０％を
上限とした。As the shape deteriorates, bits are likely to occur, and the amount of hydrogen in the weld metal increases, resulting in a significant deterioration in cold cracking resistance. On the other hand, if it exceeds 30%, the viscosity of the slag becomes insufficient, resulting in poor appearance and shape of the weld bead, and the protective cylinder becomes brittle, resulting in poor welding workability, so 30% is set as the upper limit.
（Ｍｇ ： ０．５〜５重量％〕
Ｍｇは溶接金属中の酸素量を低減し、微細炭化物の析出
促進によるＣの固定により耐割れ性を向上させると同時
に、溶接金属の延性向上に効果がある。その添加量が０
．５％未満ではその効果が得られない、他方、５％を超
えると溶接時のアークが不安定となりスパッタの発生量
が増加し溶接作業性が劣化するので５％を上限とした。(Mg: 0.5 to 5% by weight) Mg reduces the amount of oxygen in the weld metal, improves cracking resistance by fixing C by promoting the precipitation of fine carbides, and is also effective in improving the ductility of the weld metal. Yes, the amount added is 0.
．． If it is less than 5%, the effect cannot be obtained. On the other hand, if it exceeds 5%, the arc during welding becomes unstable, the amount of spatter generated increases, and welding workability deteriorates, so 5% was set as the upper limit.
なお、被覆剤に添加するＭｇはＭｇ単体の他ｊＶ −Ｍ
ｇなとの合金として添加することもできる。この場合、
合金中のＭｇの量が上記範囲内であれば同様の効果の得
られることが確認されている。In addition, the Mg added to the coating material includes Mg alone, as well as jV -M
It can also be added as an alloy with g. in this case,
It has been confirmed that similar effects can be obtained if the amount of Mg in the alloy is within the above range.
本発明の被覆アーク溶接棒は、被覆剤中に前述の成分の
他、脱酸剤としてＳｔ、 Ｍｎ、 Ｔｉ、ｊＶなど単体
金属やＦｅ−５Ｌ、 Ｆｅ−Ｍｎ、 Ｆｅ−Ｔｉ、 Ｆ
ｅ−Ｍなどの鉄合金などのいずれかを含有せしめるが、
前述の？ｔｇを含め２５％以下の範囲が脱酸および溶接
作業性の面で望ましい、なお、これら脱酸剤の添加範囲
は特に規定するものではない。The coated arc welding rod of the present invention contains elemental metals such as St, Mn, Ti, and jV, and Fe-5L, Fe-Mn, Fe-Ti, and F as deoxidizers in addition to the above-mentioned components in the coating material.
Although it contains one of iron alloys such as e-M,
The aforementioned? A range of 25% or less including tg is desirable in terms of deoxidation and welding workability, and the addition range of these deoxidizers is not particularly defined.
次に、アーク安定剤としては被覆剤中にチタンスラグ、
ルチール、鉄粉、アルカリ成分などを添加するが、その
添加範囲は合計４５％以下が望ましい。Next, titanium slag is used as an arc stabilizer in the coating material.
Rutile, iron powder, alkaline components, etc. are added, but the total addition range is preferably 45% or less.
さらに、粘結剤としては主に硅酸ソーダ、硅酸カリを含
有する水硝子を用いるが、水硝子中のＳｔａｇのモル分
率のＮａｚ０．Ｋ！０などのアルカリ成分のモル分率に
対する比が１．５〜３．５の範囲の水硝子を使用するこ
とが望ましい。Furthermore, as a binder, water glass containing mainly sodium silicate and potassium silicate is used, but the mole fraction of Stag in the water glass is Naz0. K! It is desirable to use water glass having a ratio of the mole fraction of alkaline components such as 0 to 1.5 to 3.5.
本発明の被覆アーク溶接棒は、以上述べた被覆剤を心線
の周囲に被覆剤重量が溶接棒重量に対して２５〜３５％
となるように、通常の溶接棒塗装機により被覆塗装した
後、水分を除去するため３００〜５５０℃で焼成して製
造する。The coated arc welding rod of the present invention includes the above-described coating material around the core wire, and the weight of the coating material is 25 to 35% of the weight of the welding rod.
It is manufactured by applying a coating using a normal welding rod coating machine so that the coating is applied, and then baking it at 300 to 550°C to remove moisture.
以下に本発明の効果を更に具体的に示す。The effects of the present invention will be shown in more detail below.
（実施例）
第２表に本発明被覆アーク溶接棒および比較被覆アーク
溶接棒の心線成分（各４．０謹径）、被覆剤組成とこれ
ら溶接棒による各種試験結果を示す。(Example) Table 2 shows the core components (4.0 diameter each), coating material compositions, and various test results for these welding rods of the coated arc welding rods of the present invention and the comparative coated arc welding rods.
第２表においてＡ１−Ａ１２が零発−明溶接棒であり、
８１〜Ｂ１５は比較溶接棒である。In Table 2, A1-A12 are zero invention welding rods,
81 to B15 are comparative welding rods.
これら被覆アーク溶接棒による溶着金属の４８２℃短時
間高温引張強度、伸び率および５００℃、３０００ｈｒ
におけるクリープ破断強度を求めた。また、溶接作業性
調査を行った。482℃ short-time high temperature tensile strength, elongation rate and 500℃, 3000hr of weld metal using these coated arc welding rods
The creep rupture strength was determined. We also conducted a welding workability investigation.
なお、短時間高温引張試験片およびクリープ破断試験片
を採取する溶着金属は、ＡＷＳ Ａ ５．４に準じて溶
接電流１６０Ａ、溶接入熱２５ｋＪ／ｃｍで行い、溶接
後７１０℃、３０ｈｒの後熱処理を施した後に作成した
。また、溶接作業性は溶着金属作成時と同時に調査を行
い、溶接ビード外観、形状、アーク状態、スラグ状態お
よびスラグ剥離性などの面から総合評価した。The weld metal from which short-time high-temperature tensile test pieces and creep rupture test pieces are collected was conducted at a welding current of 160 A and a welding heat input of 25 kJ/cm in accordance with AWS A 5.4, and was subjected to post-heat treatment at 710°C for 30 hours after welding. Created after applying. In addition, welding workability was investigated at the same time as weld metal preparation, and a comprehensive evaluation was made from aspects such as weld bead appearance, shape, arc condition, slag condition, and slag removability.
本発明溶接棒Ａ１〜Ａ１２はいずれにおいても５４ｋｇ
／−以上の短時間高温引張強度、２０％以上の伸び率、
また３ ３ ｋｇｆ／ａｍ”以上のクリープ破断強度さ
らに良好な溶接作業性が得られた。Each of the welding rods A1 to A12 of the present invention weighs 54 kg.
Short-time high temperature tensile strength of /- or more, elongation rate of 20% or more,
In addition, a creep rupture strength of 33 kgf/am'' or more and better welding workability were obtained.
比較溶接棒Ｂ１はＴａの添加量が不足していると同時に
金属炭酸塩が不足しているため適性な強度が得られない
とともにスラグの被包性が悪くなり、溶接ビード外観、
形状が劣化した。Comparative welding rod B1 lacks the added amount of Ta and metal carbonate, so it cannot obtain appropriate strength and has poor slag encapsulation, resulting in poor weld bead appearance and poor metal carbonate content.
The shape has deteriorated.
Ｂ２は、Ｔａの添加量と金属炭酸塩が過剰であるため溶
接金属の延性が低下するとともに、スラグの流動性が悪
くなり、溶接ビード外観、形状が劣化した。In B2, the ductility of the weld metal decreased due to the excessive amount of Ta added and the metal carbonate, and the fluidity of the slag deteriorated, resulting in deterioration in the appearance and shape of the weld bead.
Ｂ３は、脱酸剤およびＺｒの添加量が過剰であるため溶
接作業性が悪化したと同時にＴａの添加量が不足してい
たため、高クリープ破断強度が得られていない。In B3, welding workability deteriorated due to excessive amounts of deoxidizer and Zr added, and at the same time, high creep rupture strength was not obtained because the amount of Ta added was insufficient.
Ｂ４は、Ｍｎの添加量が不足したため多層盛り溶接金属
の焼入れ性が劣化し、適正な強度が得られなかった。In B4, the hardenability of the multilayer weld metal deteriorated due to insufficient addition of Mn, and appropriate strength could not be obtained.
Ｂ５は、Ｍｎの添加量が過剰であると同時にＴａが不足
しているため、高温強度および高クリープ破断強度が得
られていない。B5 does not have high temperature strength and high creep rupture strength because the amount of Mn added is excessive and at the same time Ta is insufficient.
Ｂ６は、Ｃｒの添加量が不足しているため十分な強度が
得られなかった。In B6, sufficient strength could not be obtained because the amount of Cr added was insufficient.
Ｂ７は、Ｃｒの添加量が過剰であると同時にＭｇが過剰
であるため、Ｃｒ量が適用鋼材のＣｒ量に合致しないと
ともに溶接中のスパッタの発生量が多く溶接作業性が劣
化した。In B7, since the amount of Cr added was excessive and the amount of Mg was also excessive, the Cr amount did not match the Cr amount of the applied steel material, and a large amount of spatter was generated during welding, resulting in poor welding workability.
Ｂ８は、Ｍｏの添加量が不足しているため適正な強度が
得られていない。In B8, appropriate strength was not obtained because the amount of Mo added was insufficient.
Ｂ９は、Ｍｏの添加量が過剰であると同時にＴａの添加
量が不足しているため、高温強度および高クリープ破断
強度が得られなかった。In B9, high temperature strength and high creep rupture strength could not be obtained because the amount of Mo added was excessive and the amount of Ta added was insufficient.
ＢＩＯは、■の添加量が不足しているため適正な強度が
得られていない。In BIO, appropriate strength cannot be obtained because the amount of (■) added is insufficient.
Ｂｌｌは、■の添加量が過剰であるためスラグの剥離性
、溶接作業性が劣化した。In Bll, the slag removability and welding workability deteriorated due to the excessive amount of (■) added.
Ｂ１２は、アーク安定剤であるルチールと鉄粉が過剰で
あると同時にＮｂの添加量が不足しているため、耐棒焼
は性が劣化してかえってアークは不安定になるとともに
、ＮｂＣの析出効果が得られず適正な強度が得られなか
った。B12 has an excess of rutile and iron powder, which are arc stabilizers, and at the same time an insufficient amount of Nb, which deteriorates the stick burning resistance and makes the arc unstable, as well as NbC precipitation. No effect was obtained and appropriate strength could not be obtained.
Ｂ１３は、アーク安定剤が添加されていないと同時にＮ
ｂの添加量が過剰であるため、アーク不安定となりスパ
ッタ量が増加し溶接作業性が劣化するとともに、組織が
粗大化し適正な強度が得られなかった。B13 has no arc stabilizer added and at the same time N
Because the amount of b added was excessive, the arc became unstable, the amount of spatter increased, welding workability deteriorated, and the structure became coarse, making it impossible to obtain appropriate strength.
Ｂ１４は、金属弗化物が不足していると同時にＺｒの添
加量が過剰であるため、スラグの流動性が悪く、溶接ビ
ード外観、形状が劣化した。In B14, since the amount of metal fluoride was insufficient and at the same time the amount of Zr added was excessive, the fluidity of the slag was poor and the appearance and shape of the weld bead deteriorated.
Ｂ１５は、金属弗化物が過剰であるためスラグの粘性が
不足し、溶接ビード外観、形状が劣化した。In B15, the viscosity of the slag was insufficient due to excessive metal fluoride, and the appearance and shape of the weld bead deteriorated.
＠３）Ｃ印は良好、ｘ印は不良を示す。@3) The C mark indicates good quality, and the x mark indicates poor quality.
（発明の効果）
以上の様に、本発明溶接棒は従来の２′／、〜３％Ｃｒ
−１％Ｍｏ鋼の被覆アーク溶接棒に比較し、４８２℃短
時間高温引張強度、高温延性および４５０〜５００℃に
おけるクリープ破断強度を著しく向上、かつ安定化させ
、更に優れた溶接作業性を発揮するものであり、従来の
２ｙ４〜３％Ｃｒ−１％Ｍｏ鋼溶接棒では到底達成し得
ないもので、各種産業の発展に貢献するところ極めて大
である。(Effects of the invention) As described above, the welding rod of the present invention has a Cr content of 2'/~3%
- Compared to coated arc welding rods made of 1% Mo steel, the short-time high temperature tensile strength at 482°C, high temperature ductility, and creep rupture strength at 450 to 500°C are significantly improved and stabilized, and exhibits even better welding workability. This is something that cannot be achieved with conventional 2y4-3%Cr-1%Mo steel welding rods, and it will greatly contribute to the development of various industries.
第１図は良好な短時間高温引張強度、高温延性およびク
リープ破断強度の得られるＴａ量の好適範囲を示す図で
ある。FIG. 1 is a diagram showing a preferable range of the amount of Ta that provides good short-time high-temperature tensile strength, high-temperature ductility, and creep rupture strength.
Claims (1)
してＴａ、その他にＭｎ、Ｃｒ、Ｍｏ、Ｖ、Ｎｂおよび
Ｚｒの一種または二種以上を下記に示す範囲（重量％）
で添加し、被覆剤全重量に対しアルカリ土類金属の炭酸
塩を３０〜７０％、金属弗化物を５〜３０％、Ｍｇ０．
５〜５％、その他に上記以外の脱酸剤、アーク安定剤、
粘結剤を含む被覆剤を心線の周囲に被覆したことを特徴
とする低水素系被覆アーク溶接棒。 Ｔａ：０．０１≦心線中（Ｔａ） ＋被覆剤中（Ｔａ）×０．２０≦５．０ Ｍｎ：０．１≦心線中（Ｍｎ） ＋被覆剤中（Ｍｎ）×０．１５≦１．５ Ｃｒ：２．０≦心線中（Ｃｒ） ＋被覆剤中（Ｃｒ）×０．３５≦３．５ Ｍｏ：０．８≦心線中（Ｍｏ） ＋被覆剤中（Ｍｏ）×０．３５≦１．５ Ｖ：０．４≦心線中（Ｖ） ＋被覆剤中（Ｖ）×０．２８≦１．０ Ｎｂ：０．０２≦心線中（Ｎｂ） ＋被覆、剤中（Ｎｂ）×０．２０≦０．１１Ｚｒ：０．
０５≦心線中（Ｚｒ） ＋被覆剤中（Ｚｒ）×０．５≦１．０[Claims] Either or both of the core wire and the coating material contain Ta and one or more of Mn, Cr, Mo, V, Nb and Zr in the following range (wt%):
Alkaline earth metal carbonate is added in an amount of 30 to 70%, metal fluoride is added in an amount of 5 to 30%, and Mg0.
5-5%, in addition to deoxidizers other than those listed above, arc stabilizers,
A low hydrogen-based coated arc welding rod characterized by having a core wire coated with a coating material containing a binder. Ta: 0.01≦In the core wire (Ta) + In the coating agent (Ta)×0.20≦5.0 Mn: 0.1≦In the core wire (Mn) +In the coating agent (Mn)×0.15 ≦1.5 Cr: 2.0≦In the core wire (Cr) +In the coating agent (Cr)×0.35≦3.5 Mo:0.8≦In the core wire (Mo) +In the coating agent (Mo) ×0.35≦1.5 V:0.4≦in the core (V) +in the coating (V)×0.28≦1.0 Nb:0.02≦in the core (Nb) +coating, (Nb) x 0.20≦0.11 Zr: 0.
05≦core (Zr) + coating agent (Zr) x 0.5≦1.0
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP9536590A JPH03294089A (en) | 1990-04-11 | 1990-04-11 | Low hydrogen type coated arc welding electrode |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP9536590A JPH03294089A (en) | 1990-04-11 | 1990-04-11 | Low hydrogen type coated arc welding electrode |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH03294089A true JPH03294089A (en) | 1991-12-25 |
Family
ID=14135603
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP9536590A Pending JPH03294089A (en) | 1990-04-11 | 1990-04-11 | Low hydrogen type coated arc welding electrode |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH03294089A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101890594A (en) * | 2010-07-30 | 2010-11-24 | 西安理工大学 | Low-hydrogen basic electrode for 25Cr2Ni4MoV alloy steel welding |
-
1990
- 1990-04-11 JP JP9536590A patent/JPH03294089A/en active Pending
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101890594A (en) * | 2010-07-30 | 2010-11-24 | 西安理工大学 | Low-hydrogen basic electrode for 25Cr2Ni4MoV alloy steel welding |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US6340396B1 (en) | Flux cored wire for welding duplex stainless steel | |
| JP5977998B2 (en) | Ni-base alloy weld metal, strip electrode, and welding method | |
| JP2002511023A (en) | Flux core wire for gas flow shield welding | |
| JP5097499B2 (en) | Flux-cored wire for gas shielded arc welding for low alloy heat resistant steel | |
| JPWO2005070612A1 (en) | Ni-based high-Cr alloy filler and welding rod for covered arc welding | |
| JP5928726B2 (en) | Covered arc welding rod | |
| JP3170165B2 (en) | Covered arc welding rod for Ni-based high Cr alloy | |
| JPH11347790A (en) | Coated electrode for ni group high cr alloy | |
| JP3354460B2 (en) | Covered arc welding method for high strength steel | |
| JPH06285683A (en) | Low hydrogen coated electrode | |
| JPH08257791A (en) | Low hydrogen covered electrode | |
| JPS632592A (en) | Flux cored wire for low alloy heat resistant steel welding | |
| JPH09253886A (en) | Flux cored wire for gas shielded metal arc welding for 690mpa class high tensile steel | |
| JPH03294089A (en) | Low hydrogen type coated arc welding electrode | |
| JP4309172B2 (en) | Low hydrogen coated arc welding rod for low alloy heat resistant steel | |
| JPH10272594A (en) | Low hydrogen type coated electrode | |
| JP2017170515A (en) | Flux-cored wire for gas shield arc welding | |
| JPS63242491A (en) | Low hydrogen coated electrode | |
| JPH09122972A (en) | Coated electrode for high-cr ferrite heat resisting steel | |
| JPH04305396A (en) | Low hydrogen type coated arc welding rod | |
| JPH0542390A (en) | Low hydrogen type coated electrode for welding 9cr steel | |
| JP3032988B2 (en) | Low hydrogen coated arc welding rod | |
| JPH08174267A (en) | Flux cored wire for arc welding | |
| JPH03291190A (en) | Coated arc welding electrode for welding 9cr-1mo steel | |
| JPS62224497A (en) | Low hydrogen coated arc electrode |